Method for making porous mullite-containing composites

ABSTRACT

Porous composites of mullite and cordierite are formed by firing an acicular mullite body in the presence of a magnesium source and a silicon source. In some variations of the process, the magnesium and silicon sources are present when the acicular mullite body is formed. In other variations, the magnesium source and the silicon source are applied to a previously-formed acicular mullite body. Surprisingly, the composites have coefficients of linear thermal expansion that are intermediate to those of mullite and cordierite alone, and have higher fracture strengths than cordierite at a similar porosity. Some of the cordierite forms at grain boundaries and/or points of intersection between mullite needles, rather than merely coating the needles. The presence of magnesium and silicon sources during acicular mullite formation does not significantly affect the ability to produce a highly porous network of mullite needles.

This application claims benefit of U.S. Provisional Patent ApplicationNo. 61/097,957, filed 18 Sep. 2008.

This invention relates to methods for making porous mullite-cordieritecomposite bodies.

Acicular mullite takes the form of high aspect ratio needles. Masses ofthese needles form high surface area, highly porous structures, whichare characterized by their excellent temperature resistance andmechanical strength. Porous acicular mullite bodies are used asparticulate traps to filter soot from the exhausts emitted from powerplants. The power plant may be mobile or stationary. An example of amobile power plant is an internal combustion engine. Stationary powerplants include electricity and/or steam generating units. The porousacicular mullite bodies are also useful as catalyst supports, such assupports for precious metals in automotive catalytic converters.

A convenient way of manufacturing porous acicular mullite bodies startswith a “green body” that contains a source of aluminum and siliconatoms. By heating in the presence of a fluorine source, a fluorotopazcompound having the approximate chemical formula Al₂(SiO₄)F₂ is formed.Fluorotopaz is then thermally decomposed to form mullite, which has theapproximate chemical formula 3Al₂O₃.2SiO₂. The mullite crystals formedthis way take the form of a mass of interconnected needles. The needlesusually have diameters between 3 and 40 microns. The interconnectedneedles form a porous structure in which the pores constitute from 40 to85% of the volume of the body. Approaches such as these are described inWO 90/01471, WO 99/11219, WO 03/82773 and WO 04/96729.

Acicular mullite has somewhat lower thermal shock resistance than isdesired for applications such as particulate filters and catalystsupports, mainly due to its relatively high coefficient of thermalexpansion, which is approximately 5.5 ppm per degree Celsius. Duringthermal regeneration, an acicular mullite body used in some power plantoperations can experience a temperature gradient amounting to hundredsof degrees Celsius over a period of minutes or even seconds. The poorthermal shock resistance leads to cracking under these conditions. It ispossible to ameliorate this problem somewhat through the design of thefilter. However, a more desirable approach is to improve the thermalshock resistance by focusing on the material properties of the ceramic,while maintaining other desirable attributes such as high porosity andgood mechanical integrity.

Mullite has been formed into various composites with cordierite. Forexample, U.S. Pat. No. 5,079,064 describes a composite containingmullite, cordierite and corundum phases and up to 50% of an amorphousglassy phase. That composite is made using S-glass fibers and alumina asstarting material, and results in a composite having a complex gradientstructure. These composites are said to have good thermal shockresistance. However, the composite does not have the desired highlyporous structure, and for that reason is not suitable for manyfiltration and catalyst support applications.

EP 0 164 028 and U.S. Pat. No. 5,405,514 describe adding a cordieritephase to mullite in order to match the coefficient of thermal expansionof the mullite to that of silicon. EP 0 164 028 describes a powdersintering approach to making the composite, whereas U.S. Pat. No.5,405,514 describes a sol-gel method followed by sintering. Thecomposite in these cases is a compact material that is used as asubstrate in integrated circuit devices. The bodies produced in thesemethods are not porous enough for filtration and catalyst supportapplications.

U.S. Pat. No. 5,407,871 describes a composite having a glassy phase withup to 45% of mullite particles dispersed in the glassy phase. The glassyphase includes cordierite crystallites. These composites are made bymelting calcium carbonate, aluminum hydroxide, silica, magnesiumcarbonate, boric acid and zirconia together, dropping the molten mixtureinto water to form a frit, crushing the frit to form a glass powder,mixing mullite particles into a glass powder, molding and firing. Onceagain, this process does not form bodies that have significant porosity.

A method is desired by which a porous mullite body can be prepared witha lower coefficient of linear thermal expansion (CTE). The body shouldalso have good mechanical integrity and fracture strength, and should behighly porous.

This invention is a process comprising firing an acicular mullite bodyin the presence of a source of silicon atoms and a source of magnesiumatoms at a temperature of from 1200 to 1460° C. such that a portion ofthe acicular mullite reacts with the sources of silicon and magnesiumatoms to form a composite body containing mullite and cordierite at aweight ratio of from 99:1 to 1:99, wherein the composite body containsat least 80% by weight combined of mullite and cordierite, has aporosity of at least 30-volume percent and a CTE no greater than 5.25ppm/° C. over the temperature range from 20 to 800° C.

There are two main variations on the process, which can be usedalternatively or in some combination. The variations involve the pointin the process at which the magnesium source is provided.

In the first variation, the sources of magnesium and silicon atoms arepresent when the acicular mullite body is created. This variation of theprocess comprises the steps of:

(a) forming a green body containing a source of aluminum atoms, a sourceof silicon atoms and a source of magnesium atoms;(b) heating the green body in the presence of a gaseous fluorine sourceat a temperature sufficient to convert a least a portion of the greenbody to fluorotopaz;(c) further heating the green body at a temperature from 850° C. to1250° C. under conditions such that the fluorotopaz decomposes to form aporous acicular mullite body that contains a source of magnesium atomsand a source of silicon atoms; and(d) further heating the acicular composite body to a temperature of from1200 to 1460° C. under vacuum or an inert atmosphere such that a portionof the acicular mullite reacts with the source of magnesium atoms andthe source of silicon atoms to form cordierite.

In a second variation of the process, the source of magnesium atoms and,if necessary, a source of silicon ions is applied to a previously-formedacicular mullite body. This is conveniently formed by coating theacicular mullite body by contacting it with a slurry of particles orsolution of a magnesium compound and, if necessary, a silicon compound,and drying. The coated acicular mullite body is then fired. A portion ofthe mullite reacts with the magnesium and silicon sources and isconverted to cordierite.

The ratio of mullite to cordierite that forms in either variation of theprocess can be as high as 99:1 and as low as 1:99 by weight, based onthe combined weight of those phases. This ratio preferably is at least20:80 (mullite:cordierite) and preferably does not exceed 80:20. Thecomposite may contain phases of other materials, notably various formsof silica such as cristobalite and glassy silica, and products ofincomplete reaction such as sapphirine and spinel. These other materialsmay constitute as much as 20% of the weight of the composite, butpreferably are present in significantly lesser amounts, such as 10weight percent or less, 5 weight percent or less, or 2 weight percent orless based on the weight of the composite. A crystalline silica phasesuch as cristobalite or tridymite may be present, as may a glassy silicaphase. These crystalline silica phases, especially cristobalite aregenerally undesirable. Cristobalite undergoes a crystalline phasetransition in the range of 200-250° C., which is accompanied by avolumetric expansion. This adds to the CTE of the composite and in turncan reduce the thermal shock resistance of the material. Preferredcomposites therefore contain no more than 2%, more preferably no morethan 1% and still more preferably no more than 0.5% by weight ofcristobalite. It is especially preferred that the mullite-cordieritecomposite contains no more than 2 weight percent of cristobalite, nomore than 2 weight percent of spinel and no more than 2 weight percentof sapphirine. Most preferably, the composite contains no more than 1percent, especially no more than 0.5%, each of cristobalite, spinel andsapphirine.

The composite has a lower CTE than acicular mullite alone. The CTEgenerally decreases with increasing cordierite content. Surprisingly,the CTE often approximates the theoretical CTE values that would becalculated by application of the rule of mixtures, but variations fromthe calculated value can be seen when phases other than mullite andcordierite are present. The CTE values for the composite materialstypically range from about 1.5 to about 5.25 ppm/° C., as measured overthe temperature range from 20° C. to 800° C., while heating at the rateof 5° C./minute. CTE is conveniently determined by measuring changes inthe length of a sample as it is heated over that temperature range. Adilatometer such as Du Pont model 2940 dilatometer is a convenientdevice for measuring CTE.

The large reduction in CTE through the formation of the cordierite phaseis highly desirable, but is unexpected because a continuous acicularmullite structure is either used as a starting material or formed as anintermediate. The addition of cordierite to such a structure would notbe expected to result in such a large reduction of CTE in such a case,because it would be expected that the CTE would be dominated by thecontinuous nature of the mullite needle structure. Cordierite that formsmerely on the surface of the mullite crystals in such a continuousmullite needle structure in a random fashion would be expected to havelittle effect on the CTE of a composite as a whole. In such a structure,the rule of mixtures would not be expected to be applicable, as the CTEis controlled mainly by one component of the composite, i.e., themullite needle structure, due to the expected continuity of itsstructure. Instead, and surprisingly, some of the cordierite appears toform, at least in part, between mullite grain boundaries, possibly beingconcentrated at the intersections of individual mullite needles.Although the invention is not limited to any theory, cordierite thatforms between grain boundaries is believed to contribute to thereduction in CTE by disrupting the continuity of the mullite needlestructure. This could account for the reduction of the CTE of thecomposite material compared to that of the starting acicular mullitestructure and, as said, often comes close to theoretical values thatmight be calculated from the rule of mixtures.

Another advantage of the invention is that much of the porous andneedle-like structure of the acicular mullite intermediate is retained.The resulting composite structure is in most cases highly porous, withporosities that potentially range from 30 to as much as 85 volumepercent and more typically range from 45 to 75% or from 48 to 65% oreven from 48 to 60%. The needle-like morphology of the mullite tends tobe retained in the composite, until very high cordierite concentrationsare reached, although the distinctiveness of the needles tends todecrease with increasing cordierite content. The composites are usefulin filtration and catalyst support applications due to their highporosity.

The composite also has mechanical strength that is much higher than thatof porous cordierite alone, at an equivalent porosity.

Still another advantage of the invention is that the surfaces of thebody tend to be smoother, i.e., fewer mullite needles tend to extendfrom the surface of the body, or extend less far on average from thesurface of the body, than is the case with conventional acicular mullitebodies that do not contain significant levels of cordierite. This effectis often seen even though at comparable porosities, so that surfacesmoothness is not obtained at the expense of porosity. This can be veryimportant in filter applications, because protruding needles candecrease air flow and, conversely, increase the pressures needed tooperate the filter.

In another aspect, the invention is a composite containing mullite andcordierite in a weight ratio of from 99:1 to 1:99, wherein the mulliteand cordierite constitute at least 80% of the weight of the composite,wherein the composite has a porosity of from 30 to 85 volume percent anda CTE of no greater than 5 ppm/° C. over the temperature range from 20to 800° C.

FIG. 1A is a micrograph of Comparative Sample C-5.

FIG. 1B is a micrograph of Example 18.

FIG. 1C is a micrograph of Example 19.

FIG. 1D is a micrograph of Example 20.

FIG. 2 is a micrograph of Example 32.

In the first variation of this process, acicular mullite is formed froma green body which is composed at least in part of a source of aluminumatoms, a source of silicon atoms, and a source of magnesium atoms. Thegreen body is formed in substantially the shape and dimensions requiredof the final part.

Suitable aluminum, silicon and magnesium sources include materials suchas described in WO 92/11219, WO 03/082773, WO 04/096729, EP 0 165 028and U.S. Pat. No. 5,407,871. A single material may act as a source ofboth aluminum atoms and silicon atoms or of both magnesium atoms andsilicon atoms. Examples of suitable aluminum sources include alumina andaluminum trifluoride. Various hydrated aluminum silicates such as clays,mullite and various zeolites are sources of both aluminum and siliconatoms. Crystalline silica (such as powdered quartz) is a useful sourceof silicon atoms, and can be used instead of or in addition to thehydrated aluminum silicates or mullite as the silicon source. Fumedsilica is another useful source of silicon atoms. Because of its verysmall particle size and its amorphous structure, fumed silica tends toreact more readily than crystalline silica sources, especially with themagnesium source in the cordierite-forming step. As a result, cordieritecontents in the product composite more closely approximate thetheoretical amounts when fumed silica is the silicon source, rather thancrystalline silica.

Suitable sources of magnesium atoms include, for example, magnesiumoxide, magnesium carbonate and magnesium hydroxide. An especiallypreferred precursor is a mixture of alumina, magnesium oxide and silica.

The ratio of starting materials in the green body depends on therelative proportions of cordierite and mullite that are desired in theproduct. Since cordierite formation is limited by the amount ofmagnesium that is present, it is convenient to express the number ofmoles of aluminum and silicon atoms in the starting mixture in relationto the number of moles of magnesium atoms that are present. Higherrelative amounts of magnesium tend to produce a greater proportion ofcordierite in the composite. The starting materials may contain fromabout 3.0 to 410 moles of aluminum atoms per mole of magnesium atoms,and from about 2.8 to 150 moles of silicon atoms per mole of magnesiumatoms. These ratios can lead to the formation of a composite thatcontains about 20 to 99% by weight of mullite, based on the combinedweight of the mullite and cordierite. A preferred mixture of startingmaterials contains from about 3.0 to 18 moles of aluminum atoms and from2.8 to 8.0 moles of silicon atoms per mole of magnesium atoms. Such apreferred mixture typically produces a composite containing about 20 to80% of mullite, based on the combined weight of mullite and cordierite.A more preferred starting mixture contains about 3.8 to 12 moles ofaluminum atoms and from about 3 to about 6 moles of silicon atoms permole of magnesium atoms, and typically produces a composite containingabout 30 to 70% of mullite, based on the combined weight of mullite andcordierite.

The silicon atoms may be present in the green body in asubstoichiometric amount, a stoichiometric amount, or in excess. By“stoichiometric” amount, it is meant the amount required totheoretically react with all of the aluminum and magnesium atoms in thegreen body to form mullite and cordierite. Applicants have found thatcristobalite formation tends to be reduced when silicon is present inthe green body in substoichiometric quantities, such as from 70 to 90%of the stoichiometric amount. However, an insufficiency of silicon atomscan lead to the formation of silicon-poor (relative to cordierite)magnesium-containing compounds such as sapphirine and/or spinel.

The sources of aluminum atoms, silicon and magnesium atoms suitablyconstitute from 55 to about 99 weight percent, preferably from 80 to 95weight percent of the green body, exclusive of any binders and porogenparticles that may be present.

The green body may contain various other materials, such as sinteringaids, various impurities such as are often present in natural claystarting materials, or a compound such as is described in WO 04/096729.This compound is an oxide of one or more of Ca, Fe, Na, K, Ce, Pr, Nd,Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, B, Y, Sc and La, or a compoundof one or more of the foregoing which forms an oxide when heated in air.If not an oxide, the compound may be, for example, a chloride, fluoride,nitrate, chlorate, carbonate or silicate, or a carboxylate such asacetate. More preferred compounds are those of Nd, B, Y, Ce and/or Fe. Apreferred compound is a mixture of an Nd, Ce, Fe and/or B compound witha Ca, Y, Pr, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, Sc and/or Lacompound. If the compound contains silicon (such as a silicate), theamount of silicon provided by the compound should be taken into accountin calculating the aluminum-silicon ratio and magnesium-silicon ratio inthe green body. The compound suitably constitutes at least 0.01,preferably at least 0.1, more preferably at least 0.5 and even morepreferably at least 1 percent of the weight of the green body, exclusiveof any binder or liquid that may be present. It may constitute as muchas 12 percent of the weight of the green body, but preferablyconstitutes up to 10, more preferably up to about 5 and even morepreferably up to 2 percent of the weight of the green body, exclusive ofany binder or liquid.

A binder can be, and preferably is, mixed in with the other materials tohelp bind the particles of the starting materials together until thegreen body is fired. The binder is suitably an organic polymer, whichmay be soluble in water or some other solvent. A preferred type ofbinder is a water-soluble organic polymer, especially a cellulose ether.In general, the binder may constitute from about 1 to about 10 percentof the weight of the green body. A more preferred amount is from about 2to 8 weight percent.

The green body may also contain one or more porogens. Preferred porogensinclude carbon or graphite particles. Carbon and graphite particleshaving particle sizes as described above are commercially available frommany sources. One suitable source of carbon and graphite particles isAsbury Carbons, Inc., Asbury, N.J. The carbon or graphite particlespreferably have a carbon content of at least 80% by weight, morepreferably at least 90% by weight, even more preferably at least 95% byweight and still more preferably at least 98% by weight.

The green body is made by forming a mixture of the starting materialsand shaping it. The green body can be prepared using any suitablemethod. Wet or dry methods can be used. Wet methods are preferred. In awet method, a carrier liquid such as water or an organic liquid isblended with the starting materials to form a viscous putty or pastewhich can be processed by extrusion or molding techniques. Alcohols,glycols, ketones, ethers, aldehydes, esters, carboxylic acids,carboxylic acid chlorides, amides, amines, nitriles, nitro compounds,sulfides, sulfoxides, sulfones and the like are suitable carrierliquids, although water is most preferred. The amount of carrier fluidmay affect the porosity of the composite, as larger amounts of carrierfluid occupy more of the volume of the green body. When the carrierfluid is removed, voids can form in the spaces formerly occupied by thecarrier fluid, increasing the porosity of the composite. Increasing theamount of carrier fluid can also increase the amount of shrinkage thatthe part undergoes as it is transformed from the green body to thefinished composite. Therefore, the amount of carrier fluid can be aprocess variable that can be controlled to affect to some extent certainproperties of the final product.

The starting materials can be mixed together using ball milling, ribbonblending, vertical screw mixing, V-blending, attrition milling or anyother suitable technique. The mixed materials are then formed into thedesired shape, using, for example, processes such as injection molding,extrusion, isostatic pressing, slip casting, roll compaction, tapecasting and the like. Suitable processes are described in Introductionto the Principles of Ceramic Processing, J., Reed, Chapters 20 and 21,Wiley Interscience, 1988. Binders may be burned out before the greenbody is converted to fluorotopaz and then to mullite.

If a binder or porogen is present or a wet method is used to produce thegreen body, the green body should be dried and the binder and/or porogenburnt out. The green body may be calcined prior to performing themullitization reaction. Calcination can be performed on a green bodymade in a dry method, as well. These steps are done by heating the greenbody under vacuum or in an inert atmosphere such as nitrogen or a noblegas. Binder and porogen removal can be performed at temperatures of 300to 900° C. Calcination occurs at a temperature of at least 1100° C., upto 1400° C. The calcination step is conducted for a period of timesufficient to increase the fracture strength of the green body. Theamount of time needed will depend somewhat on the part size andporosity. Typically, from 15 minutes to 5 hours is sufficient.

In the first variation of the process, the green body is converted toacicular mullite and then partially to cordierite in a three-stepprocess. In the first step, the green body is heated in the presence ofa process gas that comprises a fluorine-containing compound. This stepforms a fluorotopaz from a portion of the starting materials. In thesecond step, the fluorotopaz decomposes to form acicular mullite. In thethird step, a portion of the acicular mullite reacts with the source ofmagnesium atoms and the remaining portion of the source of silicon atomsto form cordierite. The result is a composite of mullite and cordierite.This composite may contain up to 20% by weight of other materials.

The first, fluorotopaz-forming step is performed by heating the greenbody in the presence of a process gas that contains afluorine-containing compound. The fluorine-containing compound issuitably SiF₄, AlF₃, HF, Na₂SiF₆, NaF, NH₄F, fluorocarbon-containinggas, or some mixture of any two or more thereof. SiF₄ is preferred. Thetemperature during this step may be from 700° C. to as high as 1200° C.However, temperatures of 900° C. or lower, especially 800° C. or lower,are preferred during this step, as at higher temperatures thefluorotopaz decomposition reaction can predominate. The lowertemperatures permit the fluorotopaz formation to occur separately fromthe decomposition reaction that converts fluorotopaz to mullite. It istypically preferred to heat the green body under vacuum or an inertatmosphere such as nitrogen or a noble gas until it attains atemperature of at least 500° C. Thereafter, the fluorine-containingcompound is introduced into the furnace, and heating is continued untilthe desired temperature for the fluorotopaz-forming step is achieved.

The process gas during the fluorotopaz-forming reaction may contain upto 100% of the fluorine-containing compound, but it is also possible touse a mixture that contains from 80 to 99%, especially from 85 to 95%,by weight of the fluorine-containing compound, with the remainder beingvarious gaseous by-products that form from impurities contained in thestarting materials or from the fluorotopaz-forming or mullite-formingreactions.

A flow of the process gas may be established in the furnace during thefluorotopaz-forming step. This may promote more uniform reaction ratesbetween individual bodies that are being processed together, and in somecases even within a single body, by replenishing the fluorine-containingcompound to regions of the oven from which it may have become depleted.

The partial pressure of the fluorine-containing compound in the furnacethroughout the first reaction step can be adjusted or maintained to adesired level, and/or may be allowed to vary during the course of thereaction. Control over the partial pressure of the fluorine-containingcompound allows for some control over the reaction rate, which in turnallows for some control over the temperature of the green body or bodiesduring the fluorotopaz-forming step. The partial pressure of thefluorine-containing compound may be as low as 0 torr in early stages ofthe reaction, when the fluorine-containing compound can be consumed atabout the same rate as it is fed into the reaction. The reaction vesselinstead may be maintained at a predetermined partial pressure of thefluorine-containing compound, at least during the latter stages of thefluorotopaz-forming reaction. In such a case, a typical partial pressureof the fluorine-containing compound is from 400 to 1000 torr (53.2 to133.3 kPa), especially from 400 to 750 torr 53.2 to 99.7 kPa.

It is believed that most (80% or more) or essentially all (95-100%) ofthe aluminum atoms in the green body become incorporated intofluorotopaz during the fluorotopaz-forming reaction. The body at thispoint mainly contains fluorotopaz, the magnesium source, which may havebeen converted to magnesium fluoride, and any silica (or other unreactedsource of silicon atoms) which may remain unconsumed after thefluorotopaz-forming reaction is completed. Therefore, it is believedthat little or no cordierite is formed at this stage in the process.

After the fluorotopaz is formed, the body is heated under conditionssuch that the fluorotopaz decomposes to form acicular mullite.Fluorotopaz is decomposed by further increasing the reactiontemperature, decreasing the partial pressure of the fluorine-containingcompound, or by some combination of both. Fluorotopaz releases silicontetrafluoride gas as it decomposes. This process is endothermic. Thetemperature during the fluorotopaz-decomposition step is preferably atleast 900° C., and may be as high as 1200° C. A more preferredtemperature is at least 1050° C., or at least 1100° C. The body shouldbe held at that temperature until the fluorotopaz decomposition iscomplete. The decomposition reaction is complete when the body no longerreleases silicon tetrafluoride.

The fluorotopaz decomposition reaction is generally performed in anon-oxidizing atmosphere. The fluorine-containing compound may bepresent in the process gas during this step, but the partial pressurethereof is advantageously not greater than 755 torr (100 kPa) and can beany lower value, including zero torr. The partial pressure of thefluorine-containing compound can be used as a process variable forcontrolling the size of the mullite needles that are formed during thisstep. In addition, applicants have found that the partial pressure ofthe fluorine-containing compound in this second step of the reaction caninfluence the formation of parasitic phases, especially cristobalite. Alower partial pressure of the fluorine-containing compound in thissecond step has been found to reduce the amount of cristobalite thatforms in the composite. Therefore, it is preferred to conduct thissecond step in an atmosphere that contains either none of thefluorine-containing compound or a partial pressure of thefluorine-containing compound which is no more than 250 torr (33.2 kPa),preferably from 50 to 250 torr (6.7 to 33.2 kPa) or from 50 to 150 torr(6.7 to 20 kPa). This approach to controlling cristobalite formation isa generally preferable one, as stoichiometric amounts (or more) of thesilicon source can be present in the green body. The presence of atleast stoichiometric amounts of silicon helps to minimize the formationof parasitic magnesium-containing phases such as sapphirine and spinel.

As the fluorotopaz decomposes, acicular mullite crystals form in thebody. The acicular mullite crystals are bonded together at points ofcontact to form a porous mass having essentially the same overallgeometry and dimensions as the green body. The aspect ratio of themullite crystals is typically at least 5, preferably at least 10, morepreferably at least 20. The crystals may have a mean grain diameter of 5to 50 microns.

At the end of the fluorotopaz decomposition reaction, the body containsmainly acicular mullite and the magnesium source, which is usuallyconverted to magnesium fluoride at this stage. Some unconsumed siliconsource will also be present at this stage. The body at this stage of theprocess has a porous structure that is typical of acicular mullite. Theacicular mullite in the structure takes the form of elongated needleswhich are joined together at the points where they intersect.

This acicular mullite body is further heated to produce cordierite. Thetemperature during this cordierite-forming step is suitably from 1200 to1460° C., preferably from 1300 to 1430° C. This step can be performedunder vacuum, or under an inert atmosphere (i.e., one which does notinterfere with the cordierite-forming reaction or otherwise consumemullite or cordierite) such as air, nitrogen or other inert gas. Theatmosphere may contain some moisture to facilitate the removal ofresidual fluorine during this step. During this heating step, themagnesium source, the unconsumed portion of the silica source and someof the acicular mullite react to produce the cordierite component. It ispreferred to continue the heating step until at least 90%, and morepreferably at least 98% of the magnesium atoms in the body have beenconsumed to form cordierite.

The cordierite-forming reaction consumes mullite. Generally, two molesof mullite are consumed to produce three moles of cordierite. Magnesiumatoms and silicon atoms (in addition to the silicon atoms in the mullitecrystal structure) also are needed. The amount of cordierite that formsis generally limited by the availability of both magnesium atoms andsilicon atoms. In addition, it has been found that the amount ofcordierite that forms often is somewhat less than that which ispredicted from the composition of the green body. This may be attributedin part to the fact that the reaction involves solid-state materials.The extent to which cordierite can form depends on how well themagnesium source (typically in the form of MgF₂ at this stage of theprocess) is distributed about the previously-formed acicular mullitestructure. Solid-state reactions occur only when the reactants are inclose physical proximity; if the reactants are too distant, they cannotreact even if thermodynamic conditions and accompanying kinetic factorsare favorable. Therefore, if the magnesium source is poorly distributed,localized, magnesium-rich regions can be present. These can remainunreacted or, if present in a region that is locally poor in silicon,can form parasitic magnesium compounds such as sapphirine and/or spinel.Good distribution of the magnesium source in the green body favors morecomplete conversion of the magnesium source to cordierite. This isfavored by thoroughly mixing the starting powders and using smallerparticle size powders to form the green body.

Another reason for the lower-than-expected cordierite formation may bethat, during the flurotopaz-forming reaction, the gaseousfluorine-containing compound may react with magnesium and aluminumcompounds in the body to form volatile species such as aluminumtrifluoride and magnesium difluoride. These volatile materials mayescape from the body under the conditions of thefluorotopaz-decomposition reaction, thereby depriving the body ofaluminum and especially magnesium atoms as needed to form thecordierite, resulting in less cordierite formation than expected.Reducing the partial pressure of the fluorine-containing compound duringthis step is believed to reduce the extent of this volatilization ofaluminum and magnesium compounds from the body.

It may be necessary or desirable to remove residual fluorine from thecomposite. This is conveniently accomplished by heating the composite toa temperature of at least 1200° C., such as from 1200 to 1460° C. for aperiod of time. This heating step is preferably performed in thepresence of an atmosphere that contains some water, such as moist air orother inert atmosphere which contains some quantity of moisture. Theamount of water needed in atmosphere is generally not large, and theambient humidity is usually sufficient. This heating step can beperformed simultaneously with the cordierite-forming step describedbefore, which is preferred because doing so eliminates a separateprocess step and associated costs.

In the second variation of the process, a porous, acicular mullite bodyis formed in any convenient manner, in the substantial absence of asource of magnesium atoms other than a small amount (typically not morethan 1 weight percent) that might be present as a processing aid.Typically, this is done by forming a green body containing a source ofaluminum and silicon atoms, heating it in the presence of a SiF₄ to forma fluorotopaz and then decomposing the fluorotopaz to form the acicularmullite body. A source of magnesium atoms is then applied to theacicular mullite body, and the body is heated to 1200-1460° C. undervacuum, in air, nitrogen or other inert atmosphere to convert themagnesium source and a portion of the mullite to cordierite. Aconvenient way of applying the source of magnesium atoms to the body isto soak the body in a slurry of particles or solution of the magnesiumsource, and then drying at an elevated temperature if desired. This stepcan be performed multiple times as needed to provide the desiredquantity of magnesium atoms.

Additional silicon atoms are also needed to convert mullite tocordierite. In the second variation of the process, these additionalsilicon atoms can be added when the green body is formed (byincorporating an excess of what is needed to form the acicular mullite),or after the acicular mullite body has been formed. In the latter case,the source of silicon atoms can be applied in the same manner, andoptionally at the same time, as the source of magnesium atoms.

In the second variation of the process, the amount of acicular mullite,and added magnesium source (plus any additional source of silicon atoms,if used) are advantageously such that, prior to the firing step, thestarting materials contains from about 3.0 to 410 moles of aluminumatoms per mole of magnesium atoms, and from 2.8 to 150 moles of siliconatoms per mole of magnesium atoms. As before, a preferred mixture ofstarting materials contains from about 3.0 to 18 moles of aluminum atomsand from 2.8 to 8 moles of silicon atoms per mole of magnesium atoms anda more preferred starting mixture contains about 3.8 to 12 moles ofaluminum atoms and from 3 to 6 moles of silicon atoms per mole ofmagnesium atoms.

The product of either variation of the process retains much of theporosity of the acicular mullite body. The body at this stage contains alower proportion of mullite than before the cordierite-forming step isperformed, but the needle structure is not significantly changed, atleast at low to moderate levels of cordierite in the composite. As thecordierite content increases, the structure of the mullite needles tendsto become less and less well-defined. However, the composite retainsmuch of its porosity even when the cordierite content is quite high.

The product of the process of the invention is a composite of mulliteand cordierite. The ratio of mullite to cordierite may range from 99:1to 1:99 by weight. Preferably, this ratio is from 99:1 to 80:20 and morepreferably is from 80:20 to 20:80. The ratio may be from 80:20 to 30:70,from 70:30 to 30:70 or from 70:30 to 40:60. The presence and relativeproportions of the mullite and cordierite can be determined using, forexample, X-ray methods on a sample that has been crushed to powder. Asmentioned, the measured amount of cordierite in the product composite isoften somewhat less than predicted from the ratios of startingmaterials.

A glassy oxide phase that may contain silicon and/or aluminum as well asone or more metals contributed by a sintering aid and/or otheradditional compounds as described before may also be present in thecomposite. The composite may in some cases contain products of anincomplete reaction of the starting materials. This may be causedbecause an excess of one or more of the starting materials was present.

The composite may contain small amounts of parasiticmagnesium-containing compounds, such as, for example, sapphirine(Mg₂Al₄SiO₁₀) and/or spinel. These phases form at the expense ofcordierite. Therefore, their presence in large amounts is undesirable.Preferably each of these phases constitutes no greater than 2%,preferably no greater than 1% and still more preferably no greater than0.5% of the weight of the composite.

The open porosity of the composite can range from 30 to as much as 85volume percent and more typically ranges from 45 to 75% or from 48 to60%, as measured by water intrusion methods. The choice of startingmaterials to make the acicular mullite, especially the silicon sourceand the amount of carrier fluid, can affect the porosity of thecomposite. When fumed silica is used as the silicon source, porositiescan be up to 50% greater than when powdered quartz is used. This isbelieved to be due to the large amount of carrier fluid that is neededto disperse fumed silica into the other materials when making the greenbody. When using powdered quartz as a source of silicon, porositiesgreater than about 50% typically require the presence of a porogen inthe green body, particularly when sources of silica other than fumedsilica are used in the synthesis. Porosities also tend to decreasesomewhat with increasing cordierite content. Volume average porediameter is typically less than 50 microns, and is often between 1 and25 microns. Pore diameters are measured using mercury porosimetrymethods.

The product generally has a lower CTE than acicular mullite bodies ofcomparable porosity. The product often has a CTE of no more than 5.0ppm/° C., measured over the range from 20 to 800° C. The CTE tends todecrease with increasing cordierite content. Preferred products have aCTE of from 1.5 to 5.0 ppm/° C., and more preferably from 1.5 to 4.5ppm/° C., over the range from 20 to 800° C.

The composite body also tends to have mechanical properties that areintermediate to those of acicular mullite and cordierite. An advantageof the invention is that fracture strength is increased significantly incomparison with cordierite bodies at similar porosities, mainly becausethe cordierite microstructure is not acicular. A very useful combinationof fracture strength, porosity and thermal shock resistance is oftenachieved, especially at a mullite:cordierite ratio of from 70:30 to40:60 by weight.

The ability of the composite body to withstand thermal shock gradientscan be expressed in terms of a material thermal shock factor (MTSF),which is function of fracture strength, as determined by ASTM C1161-94,CTE and Young's modulus, as measured according to ASTM C1259-98, asfollows:

MTSF=fracture strength/(CTE×Young's modulus)

The units of MTSF are ° C., with higher values indicating better thermalshock resistance. MTSF tends to increase with increasing cordieritecontent. Typical values are 200° C. or greater, up to as much as 600° C.For preferred composites that contain mullite:cordierite in a 70:30 to40:60 ratio, MTSF values are often between 200 and 550° C., depending onporosity, processing conditions, and on other factors.

Composite bodies made in accordance with the invention are useful in avariety of filtration applications, and/or as carriers for various typesof functional materials, of which catalysts are of particular interest.The thermal stability of the composite bodies makes them well suited forhigh temperature applications, such as for treating exhaust gases frommobile or stationary power plants.

The composite body can be used as a particulate filter, especially forremoving particulate matter power plant (mobile or stationary) exhaustgases. A specific application of this type is a soot filter for aninternal combustion engine, especially a diesel engine.

Functional materials can be applied to the composite body using variousmethods. The functional materials may be organic or inorganic. Inorganicfunctional materials such as metals and metal oxides, are of particularinterest as many of these have desirable catalytic properties, functionas sorbents or perform some other needed function. One method ofintroducing a metal or metal oxide onto the composite body is byimpregnating the body with a solution of a salt or acid of the metal,and then heating or otherwise removing the solvent and, if necessary,calcining or otherwise decomposing the salt or acid to form the desiredmetal or metal oxide.

Thus, for example, an alumina coating or a coating of another metaloxide is often applied in order to provide a higher surface area uponwhich a catalytic or sorbent material can be deposited. Alumina can bedeposited by impregnating the composite body with colloidal alumina,followed by drying, typically by passing a gas through the impregnatedbody. This procedure can be repeated as necessary to deposit a desiredamount of alumina. Other ceramic coatings such as titania can be appliedin an analogous manner.

Metals such as barium, platinum, palladium, silver, gold and the likecan be deposited on the composite body by impregnating the body (whichis preferably coated with alumina or other metal oxide) with a solublesalt of the metal, such as, for example, platinum nitrate, goldchloride, rhodium nitrate, tetraamine palladium nitrate, barium formate,followed by drying and preferably calcination. Catalytic converters forpower plant exhaust streams, especially for vehicles, can be preparedfrom the composite body in that manner.

Suitable methods for depositing various inorganic materials onto aporous mullite body are described, for example, in US 2005/0113249 andWO 01/045828. These processes are generally useful in relation to thecomposite body of this invention.

In an especially preferred embodiment, alumina and platinum, alumina andbarium or alumina, barium and platinum can be deposited onto thecomposite body in one or more steps to from a filter that issimultaneously capable of removing particulates such as soot, NO_(x)compounds, carbon monoxide and hydrocarbons from a power plant exhaust,such as from vehicle engines.

The following examples are provided to illustrate the invention but arenot intended to limit the scope thereof. All parts and percentages areby weight unless otherwise indicated.

EXAMPLES 1-7 AND COMPARATIVE SAMPLES C-1 AND C-2

Composite Examples 1-7 and Comparative Sample C-2 are made byhomogenizing mixtures of MgO, Al₂O₃ and crystalline SiO₂ (powderedquartz) and then pressing the resulting mixtures into round, 25-mmdiameter, 4-mm thick pellets at about 1000 kg of pressure. Ratios ofstarting materials are shown in Table 1. The pellets are heated undervacuum to 700° C. SiF₄ gas is then introduced to a partial pressure of600 torr (79.8 kPa) over the course of about one hour. The reactor isheld at 700° C. for one hour, and the temperature is then increased at arate of 1-2° C./minute until the temperature reaches 1100° C. At thetemperature of about 1030° C., the SiF₄ pressure is decreased to 500torr (166.7 kPa). The reactor is held at 1100° C. for 3 hours, holdingSiF₄ pressure constant at 500 torr (166.7 kPa) as SiF₄ evolves due tothe decomposition of fluorotopaz. The SiF₄ gas is then evacuated fromthe reactor and the temperature is lowered to room temperature.

The pellets at this point are gray in color. Surface electron microscopyshows the mullite crystals have a needle-like, highly porous morphologywith small globules wedged between the mullite needles.

The pellets are then heated to 1400° C. in air at a rate of 2° C./min,and held at that temperature for about 6 hours. The pellets are thencooled to room temperature at the rate of 3° C./minute. This operationdoes not change the size or shape of the pellets, but the pellets havelost the gray color and now appear white. X-ray diffraction analysis onpowdered portions of the pellets is performed to determine thecomposition of their crystalline components. Results are indicated inTable 1.

The water-accessible porosity and CTE of the pellets are determined ineach case, with results as indicated in Table 1.

Surface electron microscopy shows that the needle-like microstructure iswell-preserved until the cordierite content exceeds 55% by weight,although needle surfaces appear etched and crystallite edges are lesssharp than before. At cordierite contents above 55% (Examples 6 and 7),the needle morphology can still be determined, but is less predominantthan in Examples 1-5.

Comparative Sample C-1 is made in the same manner, but without anysource of magnesium atoms. Results are shown in Table 1.

TABLE 1 Example or Comparative Sample No. C-1 C-2 1 2 3 4 5 6 7 StartingMaterials Mol-% MgO 0 1.9 3.7 8.5 10.5 15.5 17.4 19.5 20.9 Mol-% Al₂O₃60 56.7 53.7 47.4 42.2 35.2 30.4 26.8 24.4 Mol-% SiO₂ 40 41.4 42.6 44.147.3 49.3 52.2 53.7 54.7 Composite Properties Wt-% Cordierite (XRD) 0 05 15 31 45 55 84 80 Wt-% Mullite (XRD) 98 99 95 85 67 47 33 14 15 Othercrystalline phase, 2 (A) 1 (A) 0 0 2 (A) 8 (A) 12 (A) 2 (B) 5 (A) wt-%(type¹) Water-accessible porosity, % 59 59 57 55 51 49 48 45 47 CTE,ppm/° C. 5.3 5.13 4.86 4.19 3.72 3.67 3.35 1.72 1.72 ¹Crystalline phasetype A is cristobalite; type B is other silica, by XRD.

In each case, a highly porous mullite structure is formed. Porosity andCTE tend to decrease with increasing cordierite content.

EXAMPLES 8-9 AND COMPARATIVE SAMPLE C-3

Examples 8-9 and Comparative Sample C-3 are made by mixing mixtures ofMgO, Al₂O₃ and fumed silica in an aqueous suspension, removing the watervia a rotary evaporator and then drying the mixture overnight at 115° C.The resulting solid mixture is ground and pressed into pellets asdescribed in the preceding examples. The pellets are convertedsequentially to fluorotopaz, acicular mullite, and mullite-cordieritecomposites following the general procedure described in previousexamples. For examples 8-9, the fluorotopaz decomposition reaction isperformed at 1100° C. The ratios of starting materials and properties ofthe resulting composites are indicated in Table 2.

TABLE 2 Example No. C-3 8 9 Starting Materials Mol-% MgO 1.9 8.5 15.5Mol-% Al₂O₃ 56.7 47.4 35.2 Mol-% SiO₂ 41.4 44.1 49.3 CompositeProperties Wt-% Cordierite (XRD) 0 12 54 Wt-% Mullite (XRD) 99 88 46Other crystalline phase, wt-% (type¹) 1 (B) 0 0 Water-accessibleporosity, % 72 72 70 CTE, ppm/° C. 5.42 4.86 3.64 ¹Crystalline phasetype A is cristobalite; type B is other silica, by XRD.

EXAMPLES 10-16 AND COMPARATIVE SAMPLE C-4

An acicular mullite body having a porosity of 69% is made according tothe general procedures described in WO 03/082773. The body is cut intorectangular pieces each weighing about 2 grams. The pieces are dippedindividually into an aqueous slurry containing 0.1 micron magnesiumoxide and silicon oxide particles, at a weight ratio of approximately1:2.75. The pieces are then dried in an oven with forced air circulationat about 120° C. The process deposits magnesium oxide and silicon oxideparticles into the spaces between the mullite. The deposition process isrepeated several times in some cases in order to obtain desiredloadings. The loading is determined by weighing the pieces before andafter the deposition process. The loading and theoretical amount ofcordierite that will be formed as a result of that loading are indicatedin Table 3.

Cordierite is formed by heating the loaded samples to 1400° C. in airfor six hours, followed by cooling to room temperature. The compositionof the resulting composites is determined by X-ray diffraction. Porosityand CTE are determined as before. The density also is determined in eachcase. Results are as indicated in Table 3.

TABLE 3 Example or Comparative Sample No. C-4 10 11 12 13 14 15 16MgO/SiO₂ 0 3.6 5.8 12.3 18.1 25.0 33.3 51.2 loading, wt-% Targeted 0 6.810.7 21.3 29.7 38.9 48.6 65.9 Cordierite Content, wt-% Actual 0 3.0 6.117.0 29.3 34.0 41.3 65.4 Cordierite Content, wt-% Porosity, % 69 67 6560 58 54 53 39 CTE, ppm/° C. 5.44 5.21 5.24 4.69 4.21 3.87 3.67 3.04Density, g/cm³ 3.15 3.11 3.10 3.02 2.96 2.91 2.86 2.75

EXAMPLES 17-21 AND COMPARATIVE SAMPLE C-5

Composite Examples 17-21 and Comparative Sample C-5 are made by dryblending mixtures of a 325-mesh size magnesia, kappa-Al₂O₃ andcrystalline SiO₂ (400 mesh size powdered quartz). The mixtures are thenmixed with water and a binder (methyl cellulose) and extruded into 65-mmlong bars having a rectangular cross-sectional shape 12.5×1.75 mm indimension. The bars are dried in air for about one week, and debinderedby heating at 1000° C. in air. The bars are then reacted to formacicular mullite and then cordierite as follows. The starting materialsused to make each of Composite Examples 17-21 and Comparative Sample C-5are shown in Table 4.

The bars are brought to a temperature of 700° C. under vacuum andstabilized at that temperature. SiF₄ is added over 5 hours to reach apressure of 200 torr (26.6 kPa), during which time fluorotopaz forms inthe bars. The reaction is then evacuated over about 2 hours, and afterabout a total of about 530 minutes, the reactor is filled with SiF₄ toabout 410 torr (54.5 kPa). After the pressure is stabilized, thetemperature is raised at the rate of 2° C./minute. When the temperaturereaches about 1000° C., the pressure is reduced to 150 torr (20 kPa) andrate of temperature rise is decreased to 1° C./minute, until atemperature of 1100° C. is achieved. The temperature and pressure arethen held steady at 1100° C. and 150 torr (20 kPa) for two hours toallow the fluorotopaz to decompose and form acicular mullite. The SiF₄pressure is then gradually lowered and the reactor cooled to roomtemperature.

The samples are then heated to 1400° C. in air for about six hours toproduce cordierite and to rid the composites of undesired fluorideresidues. The bars are then evaluated for porosity using water intrusionmethods. Fracture strength is measured on the bars according to ASTMC1161-95, using a 4-point bend test and an Instron tester. Young'smodulus is calculated according to ATSM C1259-98 by measuring flexuralfrequencies via mechanical pulse excitation methods on an J. W. LemmensMk5 instrument. MTSF is calculated from fracture strength, CTE andYoung's modulus as described before. Results are as indicated in Table4.

TABLE 4 Example or Comparative Sample No. C-5 17 18 19 20 21 StartingMaterials MgO, g 0 2.76 5.51 8.27 11.02 13.78 Al₂O₃, g 71.80 64.41 57.0249.64 42.25 34.86 SiO₂, g 28.20 32.83 37.47 42.10 46.73 51.36 Binder, g7 7 7 7 7 7 Water, mL 50 51 51 50 49 48 Expected Cordierite Content, 020 40 60 80 100 wt-% Composite Properties Wt-% Cordierite (XRD) 0 12 3355 72 88 Wt-% Mullite (XRD) 100 88 67 45 28 12 Other crystalline phase,None None None None None None wt-% (type¹) Water-accessible porosity, %58 54 53 50 49 49 CTE, ppm/° C. 5.20 4.81 4.00 3.43 2.86 2.01 FractureStrength, MPa 23 38 33 24 28 19 Young's Modulus 30 42 37 33 28 22 MTSF,° C. 146 186 219 216 337 445

The production method used to prepare Composite Examples 17-21 resultsin composites that contain essentially all mullite and cordierite.Parasitic cristobalite, sapphirine and spinel phases are essentiallyabsent from these Composite Examples. CTE values fall with increasingcordierite content, suggesting that in each case the cordierite hasinterrupted the continuous mullite crystalline needle structure.Fracture strength generally decreases with increasing cordieritecontent. The values for Comparative Example C-5 and Example 17 arebelieved to be somewhat anomalous. Modulus also decreases withincreasing cordierite content. Material thermal shock factor increaseswith increasing cordierite content.

These results show that the process of the invention can provide aporous ceramic that is characterized with very good porosity, muchbetter material thermal shock resistance than acicular mullite, and muchbetter fracture strength and modulus than cordierite.

Micrographs are taken of each of Comparative Sample C-5 and Examples 18,19 and 20. Those micrographs form FIGS. 1A, 1B, 1C and 1D, respectively.As seen in FIG. 1A, the 100% mullite material contains long needleswhich extend quite far from the surface of the material. When thecordierite content is increased to 33%, as in Example 18 (FIG. 1B), theneedle structure is maintained, but the needles at the surface tend tobe shorter, and do not protrude as far from the surface of the material.Further increases in the cordierite content, to 55% and to 72%, lead toshorter needle formation and still smoother surfaces. The smoothersurface is desirable in filter applications and other applications inwhich a fluid is to flow through the composite material. The smoothersurface builds less pressure drop through the device, allowing loweroperating pressures to be used.

EXAMPLES 22-26 AND COMPARATIVE SAMPLES C-6

Composite Examples 22-26 and Comparative Sample C-6 are made in the samegeneral method as described with respect to Composite Examples 17-21 andComparative Sample C-5, except that fumed silica is now the siliconsource. The method is modified slightly in that the fumed silica ismixed with the other ceramic powders in aqueous suspension, rather thanby dry mixing. The suspension is mixed for one hour at room temperature,and the liquid is then removed by rotoevaporation and drying at 115° C.The dried material is ground in a mortar and pestle before being formedinto bars and fired as described in Examples 17-21. Formulation detailsare provided in Table 5.

The fired bars are evaluated in the same manner as described forExamples 17-21 and Comparative Sample C-5. Results are as indicated inTable 5.

TABLE 5 Example or Comparative Sample No. C-6 22 23 24 25 26 StartingMaterials MgO, g 0 2.48 4.96 7.44 9.92 12.40 Al₂O₃, g 64.62 57.97 51.3244.67 38.02 31.38 Fumed silica, g 25.38 29.55 33.72 37.89 42.05 46.22Binder, g 6.3 6.3 6.3 6.3 6.3 6.3 Water, mL 72 70 77 77 84 93 ExpectedCordierite Content, 0 20 40 60 80 100 wt-% Composite Properties Wt-%Cordierite (XRD) 0 14 38 59 77 94 Wt-% Mullite (XRD) 98 86 62 41 23 6Other crystalline phase, 1% Silica None None None None None wt-% (type¹)Water-accessible porosity, % 67 60 60 57 53 47 CTE, ppm/° C. 5.41 4.803.98 3.04 2.21 1.91 Fracture Strength, MPa 2.3 22 20 14 13.4 16 Young'sModulus 4 20 15 14 13 17 MTSF, ° C. 114 226 310 342 490 504

These results show how the substitution of fumed silica for powderedquartz affects the properties of the composite. The cordierite contentin all cases is closer to the theoretical value than in thecorresponding Composite Examples 17-21. Porosity is also generallyhigher, which is believed to be related to the higher amount of waterused to produce the green body. Fracture strength and Young's modulusare somewhat lower, but this is believed to be attributable to thehigher porosity of these materials. As before, these results show thatthe process of the invention can provide a porous ceramic that ischaracterized with very good porosity, much better material thermalshock resistance than acicular mullite, and much better fracturestrength and modulus than cordierite.

EXAMPLES 27-31 AND COMPARATIVE SAMPLE C-7

Composite Examples 27-31 and Comparative Sample C-7 are made by dryblending mixtures of a 325-mesh size magnesia, kappa-Al₂O₃ andcrystalline SiO₂ (400 mesh size powdered quartz). In these experiments,a substoichiometric amount of silica (80% of theoretical) is present inthe green body. The starting materials used to make each of CompositeExamples 27-31 and Comparative Samples C-7 are shown in Table 6.

The mixtures are then mixed with water and a binder (methyl cellulose)and extruded into 65-mm long bars having a rectangular cross-sectionalshape 12.5×1.75 mm in dimension. The bars are dried in air for about oneweek and debindered by heating at 1000° C. in air. The bars are thenreacted to form acicular mullite and then cordierite as follows.

The bars are brought to a temperature of 700° C. and stabilized at thattemperature. SiF₄ is added to a pressure of 600 torr (79.9 kPa), duringwhich time fluorotopaz forms in the bars. The bars are maintained atthat temperature and SiF₄ pressure for about 150 minutes, and then thetemperature is increased by 3° C./minute, then 2° C./minute and finally1° C./minute until a temperature of 1100° C. is achieved. SiF₄ is spikedinto the reactor periodically for the first 300 minutes of reaction timeto maintain the reactor pressure at 600 torr (79.8 kPa). When thetemperature reaches 1000° F., the SiF₄ pressure is reduced to 500 torr(66.6 kPa). The reactor is then held steady at 1100° C. and 500 torr(66.6 kPa) SiF₄ pressure for 3 hours. The SiF₄ pressure is thengradually lowered and the reactor cooled to room temperature.

The samples are then heated to 1400° C. in air for six hours to producecordierite and to remove fluoride residues. The bars are then evaluatedfor porosity using water intrusion methods. Fracture strength ismeasured on the bars according to ASTM C1161-95, using a 4-point bendtest and an Instron tester. Young's modulus is calculated according toATSM C1259-98 by measuring flexural frequencies via mechanical pulseexcitation methods on an J. W. Lemmens Mk5 instrument. MTSF iscalculated from fracture strength, CTE and Young's modulus as describedbefore. Results are as indicated in Table 6.

TABLE 6 Example or Comparative Sample No. C-7 27 28 29 30 31 StartingMaterials MgO, g 0 2.76 5.51 8.27 11.02 13.78 Al₂O₃, g 71.80 64.41 57.0249.64 42.25 34.86 SiO₂, g 22.56 26.27 29.97 33.68 37.38 41.09 Binder, g6.61 6.54 6.48 6.41 6.35 6.28 Water, mL 48 48 48 48 48 48 ExpectedCordierite Content, 0 20 40 60 80 100 wt-% Composite Properties Wt-%Cordierite (XRD) 0 9 29 49 66 87 Wt-% Mullite (XRD) 94 90 70 49 31 10Other crystalline phase, 6 (A) 1 (A) 1 (A) 2 (C) 2, 1 (A, C) 1, 2 (A, C)wt-% (type¹) Water-accessible porosity, % 54 55 53 51 49 49 CTE, ppm/°C. 5.50 5.05 4.23 3.19 3.11 1.84 Fracture Strength, MPa 15 40 23 20 2010 Young's Modulus 19 41 29 28 27 14 MTSF, ° C. 148 191 186 223 234 373¹Crystalline phase type A is cristobalite; type B is other silica, typeC is spinel, by XRD.

The production method used to prepare Composite Examples 27-31 resultsin composites that contain mostly mullite and cordierite, with smallamounts of parasitic cristobalite and/or spinel. The presence ofsubstoichiometric levels of silicon in the green body is therefore shownto largely suppress cristobalite formation, although it may promote somespinel formation. As in previous examples, CTE values fall withincreasing cordierite content, indicating that in each case thecordierite has interrupted the continuous mullite crystalline needlestructure. Fracture strength generally decreases with increasingcordierite content. Modulus also decreases with increasing cordieritecontent. Material thermal shock factor increases with increasingcordierite content.

Once again, these results show that the process of the invention canprovide a porous ceramic that is characterized with very good porosity,much better material thermal shock resistance than acicular mullite, andmuch better fracture strength and modulus than cordierite.

EXAMPLE 32

35.50 g of kappa-Al₂O₃, 4.84 g of MgO, 0.68 g of Fe₂O₃, and 27.16 g ofpowdered quartz are homogenized in a small coffee grinder for 4 minutes.Then, 32.50 g of Asbury Grade A625 graphite is added as porogen andmixed for two additional minutes. Finally, 7.00 g of methyl cellulose isadded and mixed for about a minute. 44.0 mL of distilled water is added,and the mixture is homogenized into a paste. This paste is extruded inform of flat bars of approximate dimensions 65×12×1.8 mm and dried inair for several days. The bars are loaded into a reactor that isevacuated and heated to 700° C. SiF₄ gas is introduced over 3 hours toreach pressure of 85 torr (11.3 kPa). After an additional hour at theseconditions, temperature is increased at 2° C./min heating rate to 900°C., and at 1° C./min to 1100° C., while keeping the SiF₄ pressure at 85torr (11.3 kPa). After another 60 minutes, the reactor is evacuated,backfilled with nitrogen, and cooled to room temperature. The mullitizedbars are then heated in air to 1400° C. for 6 hrs and cooled.

A portion of the resulting product is powdered with mortar and pestle;powder XRD analysis reveals the crystalline phases of the sample contain55% mullite and 45% cordierite by weight. Porosity is measured by thewater absorption method, fracture strength by 4-point bend test, modulusby pulse excitation technique, CTE by a dilatometer at a 5° C./minheating rate between 25 and 800° C., and pore size by the mercuryintrusion method. Results are:

Porosity: 67.3±0.1%

Fracture strength: 11±1 MPa

Modulus: 6.1±0.1 GPa

CTE^((25-800° C.)): 3.88±0.09 ppm/° C.

MTSF: 450±50° C.

Average pore size: 12.4 μm

A micrograph of the product is shown as FIG. 2. As can be seen in FIG.2, the composite has a highly porous structure, in which much of theneedle-like morphology of the acicular mullite intermediate material hasbeen retained.

What is claimed is:
 1. A composite containing a mullite and cordieritein a weight ratio of from 99:1 to 99:1, based on the combined weight ofthe mullite and cordierite, wherein the mullite and cordieriteconstitutes at least 90% of the weight of the composite, and furtherwherein the composite has a porosity of from 30 to 85 volume percent anda CTE of no greater than 5.25 ppm/° C. over the temperature range from20 to 800° C.
 2. The composite of claim 1, which contains mullite andcordierite in a weight ratio of from 70:30 to 40:60, based on thecombined weight of the mullite and cordierite, the composite has a CTEof no greater than 1.5 to 4.5 ppm/° C. over the temperature range from20 to 800° C., and the composite has a material thermal shock factor ofbetween 200 and 600° C.